High Operating Temperature InAs/GaSb Superlattice Based Mid Wavelength Infrared Photodetectors Grown by MOCVD

Abstract

High operating temperature mid-wavelength InAs/GaSb superlattice infrared photodetectors with a single heterojunction structure grown by metal–organic chemical vapor deposition are reported. By inserting a fully-depleted wider-gap barrier layer between the absorber and the p-contact, “diffusion-limited” behavior has been achieved for the heterojunction “PNn” device, in contrast to the conventional pin homojunction device. The PNn device with a 50% cutoff wavelength of 4.5 $\mathsf{\mu }\mathrm{m}$ exhibited a dark current of 2.05 $\times$ 10⁻⁴ A/cm² and a peak specific detectivity of 1.28 $\times$ 10¹¹ $\mathrm{cm}·\sqrt{\mathrm{Hz}}·{\mathrm{W}}^{-1}$ at 150 K and a reverse bias of −0.1 V.

1. Introduction

Mid-wavelength infrared (MWIR) (3–5 $\mathsf{\mu }$m) detectors are desired for a variety of civilian and military applications such as industrial process monitoring, satellite reconnaissance, and night vision. One critical requirement of the MWIR detectors is the capability of high operating temperature (HOT) operation [1], which reduces the burden of cryogenic cooling significantly and leads to a reduction in size and total cost of the detector system [2]. After decades of development, Sb-based type-II superlattices (T2SLs) has proved to be a viable solution for a variety of infrared detection applications and been considered as a competitive candidate for the HOT MWIR detectors, due to their advantages of band gap tunability, flexibility of band structure engineering [3], large electron effective masses [4], and low Auger recombination [5].

The most important factor affecting the performance of the MWIR detectors at high operating temperature is the dark current, which increases dramatically as the temperature rises and leads to a high noise level. A new type of infrared detectors known as barrier detectors initially proposed by Maimon et al. [6] in 2006 have shown excellent performances in suppressing the generation–recombination (G-R) dark current. The T2SLs with their high design flexibility of band structure inject considerable vitality into the development of the barrier detectors and have motivated various heterostructures, such as the P$\pi$Mn structure [7,8], pMp structure [9], nBn structure [10,11], and pBn structure [12]. However, these structures are usually sophisticated and require a precise control of the thickness and composition. Moreover, these T2SL detectors are normally grown by molecular beam epitaxy (MBE). Although MBE technology can grow SL materials of high-quality, the high cost during mass production remains a crucial challenge.

In the III–V industry, the metal–organic chemical vapor deposition (MOCVD) is dominant in material growth because of its low-cost production and high throughput [13]. In 2011, Huang et al. have demonstrated MOCVD-grown InAs/GaSb based LWIR photodetectors on the InAs substrate, which shows a specific detectivity (D*) of about 6.78 $\times$ 10⁹ $\mathrm{cm}·\sqrt{\mathrm{Hz}}·{\mathrm{W}}^{-1}$ at 8 $\mathsf{\mu }\mathrm{m}$ at 78 K [14]. In 2019, Wu et al. reported MOCVD-grown InAs/InAsSb based MWIR photodetectors, which exhibits a peak D* of 1.4 $\times$ 10¹¹ $\mathrm{cm}·\sqrt{\mathrm{Hz}}·{\mathrm{W}}^{-1}$ and a 50% cutoff wavelength of 4.6 $\mathsf{\mu }\mathrm{m}$ at 150 K [15]. In our group, we have been using MOCVD for the growth of antimonide-based materials and devices [16,17,18]. We have proposed an Al-free unipolar barrier heterojunction named “PNn” that is suitable for MOCVD growth and have developed a series of high-performance long wavelength photodetectors with such structure. In this study, we demonstrate a MOCVD-grown MWIR detector with a relatively-simple single heterojunction PNn structure, as compared to complicated MWIR structures grown by MBE. A conventional pin homojunction device was used as reference. The PNn device with a 50% cutoff wavelength of 4.5 $\mathsf{\mu }\mathrm{m}$ exhibited a dark current (J_d) of 2.05 $\times$ 10⁻⁴ A/cm² at −0.1 V, a differential-resistance-area product (RA) at zero bias (R₀A) of 540.12 $\mathsf{\Omega }·{\mathrm{cm}}^2$, a quantum efficiency (QE) of 32%, and a peak specific detectivity of 1.28 $\times$ 10¹¹ $\mathrm{cm}·\sqrt{\mathrm{Hz}}·{\mathrm{W}}^{-1}$ at 150 K.

2. Theory and Experimental

In a photodiode, there are three main current mechanisms, namely diffusion, generation–recombination, and tunneling currents. Among them, the diffusion current is the fundamental mechanism in photodiodes, originating from thermally or optically generated minority carriers within the absorber region. The diffusion current (J_diff) in a photodiode with n-type absorber can be described by the following expression:

$$J_{diff}=\mathrm{q}{n}_i{}^2\frac{D_h}{n_D{L}_h}\tanh \frac{x_n}{L_h}\left[\exp \left(\frac{\mathrm{q}V}{\mathrm{k}T}\right)-1\right],$$

(1)

where $x_n$ is the thickness of the absorber, k is the Boltzmann constant, V is the bias voltage, q is the electric charge, $D_h$ is the diffusion coefficient of holes, $n_i$ is the intrinsic concentration of the absorber, and $L_h$ is the diffusion length of holes.

The G-R and tunneling currents occur in the depletion region. For a pin homojunction device, it is mainly troubled by the G-R current. The generation process related to mid-gap traps dominates under reverse bias. In this case, the G-R current can be described by the following simplified expression [6]:

$$J_{G-R}=\mathrm{q}\frac{1}{{\tau }_{SRH}}·n_i·W_{dep},$$

(2)

where $n_i$ is the intrinsic concentration of the depletion region, ${\tau }_{SRH}$ is the Shockley-Read-Hall (SRH) lifetime of minority carriers, and $W_{dep}$ is the depletion width. The $n_i$ has an exponential dependence on the temperature and bandgap through $~ \exp \left(-E_g/2\mathrm{k}T\right)$; therefore, the temperature and bandgap of the depletion region can have a very dramatic effect on the G-R current.

In a photodiode, there are two tunneling mechanisms: band-to-band (btb) tunneling and trap-assisted tunneling (tat) currents. These two tunneling currents can be expressed as [19]:

$$J_{btb}=\frac{{\mathrm{q}}^{3}E\left(V\right)V}{4{\pi }^2{\hslash }^2}\sqrt{\frac{2m^{*}}{E_g}}\exp \left(-\frac{4\sqrt{2m^{*}{E}_g^3}}{3\mathrm{q}\hslash E\left(V\right)}\right),$$

(3)

$$J_{tat}=\frac{{\mathrm{q}}^2{m}^{*}V{M}^2{N}_t}{8\pi {\hslash }^3}\exp \left(-\frac{4\sqrt{2m^{*}{\left(E_g-E_t\right)}^3}}{3\mathrm{q}\hslash E\left(V\right)}\right),$$

(4)

where E is the electric field, m* is effective mass, $\hslash$ is the Planck constant, $N_t$ is the activated trap density, $E_g$ is the bandgap, $E_t$ is the trap energy location, and $M$ is the matrix element associated with the trap potential. The exponential terms of the two expressions represent the tunneling probability and have similar forms, except that the former is in terms of $E_g$ and the latter is in terms of $\left(E_g-E_t\right)$. Therefore, the trap-assisted tunneling current is less sensitive to the reverse bias voltage and cannot be ignored at a small reverse bias. Consequently, the bandgap of the depletion region also has a dramatic effect on both band-to-band tunneling and trap-assisted tunneling currents, just like the G-R current.

In the PNn design, the key point is to insert a wide-gap barrier layer (N-region) between a p-type contact layer (P-region) and an n-type absorber layer (n-region). By an appropriate choice of the doping concentration and thickness of the N-region, the depletion region is all limited in the N-region, which, from the above rationale, reduces the dark current associated with the G-R and tunneling current. On the other hand, the valence band offsets between the N-region and n-region should be close to zero in order not to block the transport of photogenerated carriers. For the InAs/GaSb SL, one can change the bandgap by varying the thickness of InAs, while not changing the position of the valence band. This brings great convenience in designing heterojunction SL devices. High performance PNn structure in the LWIR region has been successfully developed [16]. In this paper, the MWIR PNn detector is presented following the same principles.

The empirical tight binding (ETB) method [20] is used to calculate the bandgap, conduction band ($E_C$), and valence band ($E_V$) energies. The GaSb-type interfaces were used in our ETB model. The band diagrams of pin and PNn devices are shown in Figure 1. The pin device is comprised of 9 monolayer InAs/8 monolayer GaSb (9 ML/8 ML) SL designed for a cutoff wavelength of 5 $\mathsf{\mu }\mathrm{m}$ (~248 meV). In the PNn structure, the P-region and N-region are comprised 6 ML/8 ML SL with a bandgap of 357 meV, while the n-region is comprised of 9 ML/8 ML SL, same as the pin device. In the PNn design, the N-region and n-region have the same GaSb sublayer thickness (8 MLs) so that there is no discontinuity in the valance band to block the photocurrent.

The pin and PNn devices were grown on n-type InAs substrates by MOCVD. GaAs-type interfaces were formed to compensate the compressive strain from the GaSb layers. The other growth details can be found elsewhere [21]. The epitaxial structures of both devices are shown in Figure 2. The pin structure includes a 100 nm thick n-MWSL contact layer doped to 2 $\times$ 10¹⁸ cm⁻³, a 1.7 um thick unintentionally (uid) doped MWSL absorber, a 200 nm thick p-MWSL contact layer doped to 2 $\times$ 10¹⁶ cm⁻³, a 20 nm thick p-GaSb cap doped to 2 $\times$ 10¹⁶ cm⁻³. The PNn structure consisted of a 100 nm thick n-MWSL contact layer doped to 2 $\times$ 10¹⁸ cm⁻³, a 1.7 $\mathsf{\mu }\mathrm{m}$ thick n-region doped to 2 $\times$ 10¹⁶ cm⁻³, a 200 nm thick N-region doped to 4 $\times$ 10¹⁶ cm⁻³, a 250 nm thick P-region doped to 1 $\times$ 10¹⁸ cm⁻³, a 20 nm thick p-GaSb layer doped to 1 $\times$ 10¹⁸ cm⁻³. In the PNn device, the depletion region will be just within the N-region with such thickness and doping level. The undoped InAs/GaSb (9 ML/8 ML) SL absorber could be p-type in nature since undoped InAs is n-type, undoped GaSb is p-type with similar background level, and they will compensate each other, which brings uncertainty; thus, for the PNn device to work, the absorber is intentionally doped to 2 $\times$ 10¹⁶ cm⁻³. The carrier concentrations were verified by Hall measurement using lift-off test method. For material characterization and device fabrication, X-ray diffraction (XRD) was used to evaluate the structural quality of the SLs. The mesa was defined by wet chemical etching using a solution of citric acid and phosphoric acid. Sidewalls were passivated by SU-8 photoresist, and the ohmic contacts were formed by Ti/Pt/Au metal stacks. No antireflection coating was applied to the devices.

3. Results and Discussion

Figure 3 shows the XRD curves in $\omega$-2$\theta$ scan mode around InAs (004) for the pin and PNn devices. The periods for the MWSL absorbers are measured to be 5.19 nm and 5.11 nm for the pin and PNn devices, respectively, which match well with the designed thickness of 5.2 nm. Intense satellite peaks of the MWSLs were clearly observed and the full widths at half-maximum (FWHMs) of the MWSLs ± 1th order peaks were below 100 arcsec for both pin and PNn devices, suggesting a good SL structural quality.

The J_d and RA as a function of the bias voltage of the two devices at 150 K are shown in Figure 4a. A dark current density of 2.05 $\times$ 10⁻⁴ A/cm² and 5.35 $\times$ 10⁻³ A/cm² was measured at −0.1 V for the PNn and the pin devices, respectively. R₀A values are 150 K for the PNn and the pin devices are 540.12 $\mathsf{\Omega }·{\mathrm{cm}}^2$ and 13.74 $\mathsf{\Omega }·{\mathrm{cm}}^2$, respectively. It can be seen that dark current is effectively suppressed in the PNn structure. The diffusion and G-R dark currents increase as the temperature rises but in different ways. The diffusion current is proportional to $\exp \left(-E_g/\mathrm{k}T\right)$, whereas the G-R current is proportional to $\exp \left(-E_g/2\mathrm{k}T\right)$. To investigate the limiting mechanisms of the PNn and pin devices, temperature dependent current–voltage measurements were performed. Figure 4b presents the Arrhenius plot of the dark current density of the PNn and pin devices at −0.1 V applied bias. In the temperature range of 100 to 160 K, the measured dark current of the PNn device can be fitted perfectly with an activation energy of about 236 meV, which is very close to the designed n-region bandgap of 248 meV. It means that the dominant mechanism of dark current in the PNn device is the diffusion current. In comparison, the activation energy of the pin device was extracted to be 187 meV within a temperature range of 130 K to 160 K. This value is about three-fifths of the estimated bandgap energy of the 9 ML/8 ML SL, which implies the dark current mechanism involves both the diffusion and G-R currents. At 80~100 K, the dark current is only slightly sensitive to temperature and the activation energy is about 61 meV, indicating that the trap-assisted tunneling current is dominant. However, the trap-assisted tunneling current becomes insignificant and comparable to the surface contribution at small reverse bias and low temperatures; therefore, the small activation energy may also result from surface leakage.

The spectral response ($R_{\lambda }$) of the detectors was measured by the Nicolet IS50 FTIR system, calibrated by a 600 K blackbody source. The measurements were carried out under −0.1 V bias. The spectral responsivity versus wavelength at 150 K for the PNn and pin devices is shown in Figure 5. At 150 K, the PNn and pin devices exhibit a 50% cutoff wavelength of 4.5 $\mathsf{\mu }\mathrm{m}$ and 4.7 $\mathsf{\mu }\mathrm{m}$, respectively. The 100% cutoff wavelength for both devices is around 5 $\mathsf{\mu }\mathrm{m}$, which is close to the design. A peak responsivity of 1.11 A/W and 2.06 A/W was achieved for the PNn and pin devices, respectively, corresponding to a quantum efficiency (QE) of 32% and 65%. The peak response of the PNn device is much lower than in the pin device, which is attributed to the higher doping level in the PNn device and thus a decreased minority diffusion length [3]. A possible potential barrier in the valence band may also account for the lower QE.

After the electrical and optical characterizations, the specific detectivity at −0.1 V of the PNn and pin devices was calculated using the following equation:

$$D^{*}=R_{\lambda }{\left(2\mathrm{q}{J}_d+\frac{4\mathrm{k}T}{RA}\right)}^{-\frac{1}{2}}$$

(5)

where q is the electric charge, $J_d$ is the dark current density, T is the temperature of the device, k is Boltzmann constant, and R and A are dynamic resistance and diode area, respectively. The calculated D* spectra for the PNn and pin devices at −0.1 V and 150 K are provided in Figure 6, and the device results are summarized in

Table 1. Summary of the device results at 150 K.

Device	${\mathit{J}}_{\mathit{d}}\mathbf{at}-0.1\mathbf{V}(\mathbf{A}/\mathbf{c}{\mathbf{m}}^2)$	R0$\mathit{A}\left(\mathbf{\Omega }\mathit{·}\mathbf{c}{\mathbf{m}}^2\right)$	$\mathbf{Peak}{\mathit{R}}_{\mathit{\lambda }}(\mathbf{A}/\mathbf{W})$	Peak QE	$\mathbf{Peak}\mathit{D}*\left(\mathbf{c}\mathbf{m}\mathit{·}\sqrt{\mathbf{H}\mathbf{z}}\mathit{·}{\mathbf{W}}^{-1}\right)$
PNn	2.05 × 10−4	540.12	1.11	32%	1.28 × 1011
pin	5.35 × 10−3	13.74	2.06	65%	4.8 × 1010
Reference [10]	2 × 10−5 (147 K)	/	/	59%	4.6 × 1011
Reference [15]	1.6 × 10−4	356	1.23	41%	1.4 × 1011

. The peak D* reaches 1.28 $\times$ 10¹¹ $\mathrm{cm}·\sqrt{\mathrm{Hz}}·{\mathrm{W}}^{-1}$ for the PNn device, which is significantly higher than that of the pin device and comparable with those reported for MBE-grown devices with advanced design at similar cutoff wavelengths, with D* ranging from 3.4 $\times$ 10¹⁰ $\mathrm{cm}·\sqrt{\mathrm{Hz}}·{\mathrm{W}}^{-1}$ to 7.1 $\times$ 10¹¹ $\mathrm{cm}·\sqrt{\mathrm{Hz}}·{\mathrm{W}}^{-1}$ [7,8,9,10,12,22,23]. The results of Refs. [10,15] are also shown in the Table 1. It can be seen that there is still substantial room for improvement in both optical and electrical performance of the PNn device. The relatively low QE of the PNn device can be improved by lowering the doping level [24]. A further improvement of the device performance can be expected if a p-type absorber and corresponding double heterostructure structure can be used. By using the p-type absorber, the minority carriers are electrons, which have a higher carrier lifetime leading to an improved QE and reduced diffusion current. Moreover, eliminating potential barriers by optimizing the device structure and doping concentration is also a feasible direction to improve the QE of the device.

4. Conclusions

In summary, we have investigated mid-wavelength InAs/GaSb SL infrared photodetectors with an Al-free single heterojunction design and a pin homojunction design grown by MOCVD. Their performances have been compared by electrical and optical characterizations. In the PNn heterojunction, a wider-gap barrier layer was inserted between the absorber and the p-contact. XRD scan shows reasonably good structural quality for both devices. Arrhenius plots of the dark current of the PNn device were compared with the pin device. In the temperature range of 100 K to 160 K, the PNn and the pin devices demonstrated an activation energy of 230 meV and 187 meV, respectively, indicating that the PNn structure has successfully suppressed the G-R current and achieved a diffusion-limited behavior, while the pin device is dominated by both the G-R current and diffusion current. At 150 K, the pin device shows a peak QE of 65% and the PNn device shows a peak QE of 32% due to the intentionally-doped n-type absorber. At 150 K and a bias voltage of −0.1 V, the PNn device with a 50% cutoff of 4.5 $\mathsf{\mu }\mathrm{m}$ shows a dark current density of 2.05 $\times$ 10⁻⁴ A/cm² and a peak D* of 1.28 $\times$ 10¹¹ $\mathrm{cm}·\sqrt{\mathrm{Hz}}·{\mathrm{W}}^{-1}$.